EP0977212B1 - Méthode de fabrication de nanoparticules en métaux de transition - Google Patents
Méthode de fabrication de nanoparticules en métaux de transition Download PDFInfo
- Publication number
- EP0977212B1 EP0977212B1 EP99305759A EP99305759A EP0977212B1 EP 0977212 B1 EP0977212 B1 EP 0977212B1 EP 99305759 A EP99305759 A EP 99305759A EP 99305759 A EP99305759 A EP 99305759A EP 0977212 B1 EP0977212 B1 EP 0977212B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- nanoparticles
- temperature
- cobalt
- metal
- forming
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
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Images
Classifications
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- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/16—Making metallic powder or suspensions thereof using chemical processes
- B22F9/18—Making metallic powder or suspensions thereof using chemical processes with reduction of metal compounds
- B22F9/24—Making metallic powder or suspensions thereof using chemical processes with reduction of metal compounds starting from liquid metal compounds, e.g. solutions
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- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/05—Metallic powder characterised by the size or surface area of the particles
- B22F1/054—Nanosized particles
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/17—Metallic particles coated with metal
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/16—Making metallic powder or suspensions thereof using chemical processes
- B22F9/30—Making metallic powder or suspensions thereof using chemical processes with decomposition of metal compounds, e.g. by pyrolysis
- B22F9/305—Making metallic powder or suspensions thereof using chemical processes with decomposition of metal compounds, e.g. by pyrolysis of metal carbonyls
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y25/00—Nanomagnetism, e.g. magnetoimpedance, anisotropic magnetoresistance, giant magnetoresistance or tunneling magnetoresistance
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y30/00—Nanotechnology for materials or surface science, e.g. nanocomposites
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B23/00—Obtaining nickel or cobalt
- C22B23/04—Obtaining nickel or cobalt by wet processes
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/0036—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties showing low dimensional magnetism, i.e. spin rearrangements due to a restriction of dimensions, e.g. showing giant magnetoresistivity
- H01F1/0045—Zero dimensional, e.g. nanoparticles, soft nanoparticles for medical/biological use
- H01F1/0054—Coated nanoparticles, e.g. nanoparticles coated with organic surfactant
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
- H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
- H01F1/06—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys in the form of particles, e.g. powder
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/44—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of magnetic liquids, e.g. ferrofluids
- H01F1/442—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of magnetic liquids, e.g. ferrofluids the magnetic component being a metal or alloy, e.g. Fe
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y40/00—Manufacture or treatment of nanostructures
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10S—TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10S516/00—Colloid systems and wetting agents; subcombinations thereof; processes of
- Y10S516/922—Colloid systems having specified particle size, range, or distribution, e.g. bimodal particle distribution
Definitions
- the present invention relates to nanoparticle of transition metals, and more particularly to convenient chemical syntheses of stable, monodisperse elemental (such as hexagonal close-packed (hcp), face-centered Cubic (fcc), and a cubic phase of cobalt, alloy (Co/Ni, NiFe, Co/Fe/Ni,) (where relative concentrations of the elements can vary continuously) and intermetallic (Co 3 Pt, CoPt, CoPt 3 , Fe 3 Pt, FePt, FePt 3 etc.
- stable, monodisperse elemental such as hexagonal close-packed (hcp), face-centered Cubic (fcc), and a cubic phase of cobalt, alloy (Co/Ni, NiFe, Co/Fe/Ni,) (where relative concentrations of the elements can vary continuously) and intermetallic (Co 3 Pt, CoPt, CoPt 3 , Fe 3 Pt, FePt, FePt 3 etc.
- overcoated magnetic nanocrystals e.g., particles consisting of a concentric shell of material of different chemical composition produced by a serial process
- overcoated magnetic nanocrystals e.g., particles consisting of a concentric shell of material of different chemical composition produced by a serial process
- Magnetic properties of fine particles are different from those of bulk samples due to a "finite size" effects.
- Potential applications of small magnetic particles include not only ultra-high density recording, nanoscale electronics, and permanent magnets, but also their use as novel catalysts, in biomolecule labeling agents and as drug carriers.
- An important goal related to each of these potential applications is to make monodisperse magnetic domains with high durability and corrosion resistance.
- Ferromagnetic uniaxial Cobalt-based nanomaterials e.g., many of these materials are tetragonal crystal structures which like the hcp structure is uniaxial
- fcc cobalt-based nanoparticles or Ni/Fe alloy particles are magnetically soft materials with low anisotropy which is advantageous in the development of read heads and in magnetic shielding applications.
- hexagonal close-packed (hcp) and face- centered cubic (fcc) refer to the specific internal crystal structure of the particles and is important determining the anisotropy of the magnetic properties. Additionally, these materials are anticipated to display interesting, giant (e.g., very large) magnetoresistive properties when organized in extended arrays, and thus are candidates, for example, for magnetoresistive read head sensors.
- a magnetic colloid e.g., ferrofluid
- All of the above-mentioned techniques have been practiced for-many years and have been unable to refine the level of control needed for the production of stable magnetic colloids of transition metals and metal alloys to the levels demonstrated by the present inventors.
- the method of forming nanoparticles comprises steps : forming a metal precursor solution, introducing a surfactant, precipitation of nanoparticles and adding a hydrocarbon solvent.
- the conventional techniques have been unable to exercise the required control in the production of stable magnetic colloids of transition metals and metal alloys.
- the poor chemical stability of the conventional metal particle has limited the reliability of systems in which they are incorporated and has prompted wide-scale use of the metal oxide nanoparticles in many applications despite the weaker magnetic properties inherent in the metal oxide particles.
- an object of the present invention is to provide an inexpensive chemical process for preparing stable monodisperse elemental, intermetallic, alloy and over-coated nanocrystals.
- Another object of the present invention is to provide nanocrystalline materials with precisely controlled size and monodispersity for magnetic recording applications such as for magnetic storage application (recording media, as well as read and write heads).
- Yet another object of the present invention is to make a ferrofluid.
- the present inventors have developed expensive and very convenient processes for the preparation of monodisperse magnetic elemental and alloy nanoparticles such that high-quality magnetic nanocrystals have been achieved.
- the invention provide a method of forming nanoparticles according to claim 1.
- the invention includes the steps of: forming a metal salt precursor solution containing surfactant (optimally a nonionic surfactant (e.g., tertiary organophosphine) and anionic surfactant (e.g., carboxylate) in a non-reactive solvent, injecting an agent into the solution to reduce the metal salt in situ producing colloidal metal particles; adding a flocculent to cause nanoparticles to precipitate out of solution without permanent agglomeration and separating the by-products of the synthesis which remain in solution; and adding a hydrocarbon solvent to the precipitate to either redisperse or repeptize the purified nanoparticles.
- surfactant optically a nonionic surfactant (e.g., tertiary organophosphine) and anionic surfactant (e.g., carboxylate)
- injecting an agent into the solution to reduce the metal salt in situ producing colloidal metal particles adding a flocculent to cause nanoparticles to precipitate out
- the invention comprises the steps of: forming a metal precursor solution of transition metal complex at a first temperature; forming a surfactant solution which is heated to a temperature higher than the first temperature; injecting the metal precursor solution to the warmer surfactant solution, resulting in production of colloidal metal particles; adding a flocculent to the mixture to cause nanoparticles to precipitate out of solution without permanent agglomeration; and adding a hydrocarbon solvent to either redisperse or repeptize the nanoparticles.
- hexagonal close packed cobalt particles are synthesized by use of long chain (e.g., C8-C22) dihydric alcohols (e.g., diol) to reduce cobalt salts (e.g., carboxylate such as acetate) or beta-dikenonates (e.g., acetylacetonate).
- cobalt salts e.g., carboxylate such as acetate
- beta-dikenonates e.g., acetylacetonate
- Face-centered cobalt nanocrystals are obtained via thermal decomposition of zero valent cobalt complexes (e.g., cobalt carbonyls and cobalt organophosphine complexes), for example.
- Novel cubic phase cobalt nanoparticles are prepared through a superhydride reduction of cobalt salts.
- cobalt particles are stabilized by a combination of long chain caboxilic acid (e.g., C8-C22) and optimally oleic acid and trialkylphosphine.
- This stabilization is effective such that the particles can be handled easily, either in solution phase or as solid form under air.
- the particles are easily redispersible in a range of common aprotic solvents (e.g., ethers, alkanes, arenes, and chlorinated hydrocarbons).
- size-selective precipitation isolates to monodisperse nanocrystal fractions from the original distribution.
- non-solvent e.g., alcohol
- the present invention also is useful in producing Ni, Cu, Pd, Pt, and Ag nanoparticles.
- the invention produces binary intermetallic compounds (Co 3 Pt, CoPt, CoPt 3 , Fe 3 Pt, FePt, and FePt 3 ) and binary alloys (e.g., Co/Ni, Ni/Fe, and Co/Fe) and ternary alloys (e.g., Co/Fe/Ni).
- the invention also produces over-coated (e.g., such as Co-Ag and Co-Pt) nanostructured particles.
- an inexpensive chemical process is provided for preparing stable monodisperse elemental, intermetallic, alloy, and over-coated magnetic nanocrystals. Further, nanocrystalline materials are efficiently produced with controlled size and monodispersity for magnetic recording applications such as for magnetic recording media, read and write heads, and a ferrofluid is inexpensively produced.
- the present invention provides an improved procedure for preparing monodisperse magnetic colloids (e.g., ferrofluids) comprised essentially of nanometer-sized (e.g., substantially within a range of about 1 to about 20 nm) single crystals (e.g., nanocrystals) of elemental cobalt, nickel, or iron, intermetallic (e.g., CoPt and FePt) or alloys (e.g., binary alloys such as Co/Ni, Co/Fe, and Ni/Fe, and ternary alloys such as Co/Fe/Ni or the like), a colloidal stabilizer, and an organic carrier fluid.
- monodisperse magnetic colloids e.g., ferrofluids
- nanometer-sized e.g., substantially within a range of about 1 to about 20 nm
- single crystals e.g., nanocrystals
- intermetallic e.g., CoPt and FePt
- alloys e.g.
- some of the innovations include: 1) controlling nucleation phenomena by rapid injection (e.g., for purposes of the present application, rapid represents the total delivery of the reagents in less than five seconds, and more optimally between 0.5 and 2 sec) of solution containing at least one of the essential reagents for reaction into a flask containing a hot solution of all other necessary reagents which are being vigorously stirred under an inert gas atmosphere (e.g., preferably Ar, He or N 2 ); 2) adding a tertiary alkylphosphine or arylphosphine to mediate the metal particle growth; (3) changing the constitution of the reaction medium to allow controlled growth at temperatures higher than the standard procedures to improve crystalline quality of the individual nanocrystals; and 4) employing size-selective precipitation and centrifugation after the initial stages of the synthesis to narrow the particle size distribution to less than 10% (and optimally less than 5%) standard deviation in diameter.
- an inert gas atmosphere e.g., preferably
- the above-mentioned innovations may be employed individually, or in combination, to improve control of the composition and performance of the ferrofluid in addition to providing a medium from which high quality magnetic nanocrystals can be isolated.
- the present invention is an inexpensive and efficient process for preparing monodisperse magnetic elemental and alloy nanoparticles such that high-quality magnetic nanocrystals are formed.
- hexagonal close packed (hcp) cobalt particles for example, are synthesized by long chain dihydric alcohol (e.g., diol) reduction of cobalt acetate, thereby to obtain face-centered cobalt (fcc) nanocrystals, for example, via thermal decomposition of dicobalt octacarbonyl.
- Novel cubic cobalt nanoparticles are prepared through a superhydride reduction of cobalt salts.
- cobalt particles are stabilized by a combination of oleic acid and trialkylphosphine, which is effective such that the particles are handled easily either in solution phase or as solid form under air.
- the particles are easily redispersed in aprotic solvent.
- size-selective precipitation e.g., preferably by adding non-solvent alcohol to the alkane solution of the particles
- the present invention also is useful in producing Ni, Cu, Pd, Pt, and Ag nanoparticles, as described below.
- the invention produces intermetallics (e.g., CoPt, FePt), binary alloys (e.g., Co/Ni, CoFe, and Fe/Ni) and ternary alloys (e.g., Co/Fe/Ni), and over-coated (e.g., such as Co-Ag, Co-Pt, and FeNi-Ag) particles.
- intermetallics e.g., CoPt, FePt
- binary alloys e.g., Co/Ni, CoFe, and Fe/Ni
- ternary alloys e.g., Co/Fe/Ni
- over-coated particles e.g., such as Co-Ag, Co-Pt, and FeNi-Ag particles.
- an inexpensive chemical process is provided for preparing prepare stable monodisperse elemental, intermetallic, over-coated and alloy magnetic nanocrystals. Further, nanocrystalline materials are efficiently produced with controlled size and monodispersity for magnetic recording applications such as for disk and head media, and a ferrofluid is inexpensively produced.
- trialkylphosphine is chosen as one stabilizing ligand because it is a well-known ligand to stabilize zero valent metal due to a ⁇ -donating and ⁇ -back bonding characteristics.
- phosphines can be used such as symmetric tertiary phosphines (e.g., tributyl, trioctyl, triphenyl, etc.) or asymmetric phosphines (e.g., dimethyl octyl phosphine). These phosphines may be employed singly or if the situation warrants can they be used together. However, the inventors have found that trialkylphosphines reduce the particle's growth rate, but do not prevent the particle from growing to undispersable aggregates (e.g., greater than 20 nm. at temperatures between 100°C and 350°C).
- the surfactant comprises an organic stabilizer which is a long chain organic compound that may be expressed in the form R-X where:
- oleic acid is a well-known surfactant in stabilizing colloids and has been used to protect iron nanoparticles.
- Similar long chain carboxylic acids, such as erucic acid and linoleic acid also have been used in addition (e.g., any long chain organic acid with between 8 and 22 carbon atoms may be employed singly or in combination) to oleic acid.
- Oleic acid is typically preferable because it is easily available inexpensive natural sources (e.g., olive oil).
- carboxylic acid alone cannot protect the growing Co particles for optimum growth.
- phosphines and organic stabilizers offer good control on particle growth and stabilization.
- Phenylether or n-octylether are preferably used as the solvent due to their low cost and high boiling point although di-decyl and di-dodecylether can be employed.
- the reaction can be performed at temperatures ranging from 100°C to 360°C depending on the nanoparticles needed and boiling point of the solvent, and more preferably at ⁇ 240°C. If the temperature is lower than this temperature range, the particles do not grow. If the temperature is above this range, the particles grow uncontrolled with increased production of undesirable by-products.
- a polyol process involves the reduction of metal salts by diols.
- the common procedure involves dissolving the metal precursors in the neat diol and heating to initiate reduction of metal salts and produce particles. There is no temporally discrete nucleation step and little or no size control.
- the polyol process has been used to reduce metal salts including cobalt acetate to metal particles.
- Ethylene glycol is the most often used as the reducing agent.
- the reduction takes hours (e.g., typically hours) to occur and stabilization of the particles is difficult except for the late transition metal, such as Ag, Pt and Pd particles which are relatively chemically inert.
- the final product contains both hcp and fee phases of cobalt.
- long chain diols such as 1,2-octanediol, 1,2-dodecanediol and 1,2-hexadecanediol have higher boiling points (e.g., 200-300°C as compared to the boiling point for ethylene glycol of 200°C) and, if used at reflux, the long chain diols can easily and quickly reduce metal salts.
- reduction of cobalt acetate by these diols at 200 - 240°C finishes within 20 minutes.
- the most significant improvement provided by using the long chain diols is that these molecules, when dissolved in the high boiling solvent, allow the particles to remain dispersed during synthesis.
- the synthesis began with an injection of a reducing agent or an ether solution of dicobalt octacarbonyl in the presence of long chain carboxylic acid (e.g. C8-C22) and trialkylphosphine.
- a reducing agent or an ether solution of dicobalt octacarbonyl in the presence of long chain carboxylic acid (e.g. C8-C22) and trialkylphosphine.
- the introduction of the reagents by injecting preferably should be a single injection lasting less than 5 seconds for the delivery of the entire contents.
- the reduction or decomposition occurred in a short time (e.g., about 10 minutes), leading to a temporally discrete homogeneous nucleation.
- the growth of the particles was finished in less than 30 minutes such that cobalt or other metals and their alloy particles could be handled without inert atmosphere protection.
- the method of the present invention in growing the nanoparticles is very efficient (e.g., on the order of much less than the conventional methods).
- size-selective precipitation was performed by titrating the hexane solution of the particles with non-solvent ethyl alcohol and providing substantially monodisperse cobalt nanocrystals which could be easily redispersed in alkane solvent.
- the crystal phase of the final product was determined by X-ray powder diffraction, and selected are electron diffraction. There are only two stable phases known for elemental cobalt at ambient pressures. The hcp form is stable at temperatures below 425°C, while the fcc form is the stable structure at higher temperatures.
- Figure 1 illustrates an X-ray pattern of hcp cobalt nanocrystals produced with the above method according to the invention.
- the broadening of the reflection line widths as the sample size decreases in referred to as a finite size broadening.
- Figure 1 shows the X-ray diffraction pattern of a fcc cobalt nanocrystal sample confirming the bulk fcc lattice spacings.
- the X-ray pattern of the particles from superhydride reduction do not match either hcp or fcc cobalt phase, as shown in Figure 2, but display the same symmetry as the uncommon ⁇ phase of Mn metal.
- the pattern fits well to symmetry of the ⁇ -Mn structure scaled for the difference in the size of the Mn and Cobalt atoms. However, this structure is not stable at temperatures above 300°C.
- This thermal instability can be exploited to provide a simple route to convert the nanocrystals internal structure to either the fcc or hcp forms, thus changing the magnetic anisotropy. Heating this novel cubic phase can be changed to hcp cobalt phase at 300°C and fcc cobalt at 500°C. No distinct peaks corresponding to CoO and CoP phase are detected from X-ray analysis, and elemental analysis shows phosphorus incorporation is below 3%.
- different particle sizes can be prepared with smaller particles favored by a high ratio of the stabilizer/surfactant to the metal precursor solution.
- reduction of two equivalent (e.g., molar ratio) of the cobalt source in the presence of one equivalent of trialkylphosphine and one equivalent of oleic acid leads to particles up to approximately 13 nm
- more equivalent of oleic acid and trialkylphosphine e.g., a greater than 2:1:1 ratio of the metal source to the trialkylphosphine and oleic acid
- smaller particles are obtained.
- There is no specific lower limit of the particle size but the smallest cobalt containing species have too few atoms to a have a well-formed internal lattice and more closely resemble molecular species.
- the inset 100 of Figure 1 illustrates a series of X-ray patterns of hcp cobalt particles thus prepared. Annealing the particles at 300°C in vacuum results in the loss of stabilizing ligands yielding an insoluble mass of larger nanocrystal whose diffraction pattern is displayed in waveform f of inset 100. The particles diffuse and grow at this annealing condition as shown in the X-ray diffraction patterns (e.g., see inset 100 of Figure 1), and become very air-sensitive. If the sample is exposed to air, cobalt oxide particles are obtained instantly.
- a drop of octane or dodecane solution containing ⁇ 500 ppm of the product is dropped onto a carbon-coated copper grid.
- the drop of the colloid is placed onto a carbon-coated copper TEM grid.
- the solution is allowed to slowly evaporate at ambient temperature and pressure.
- the grid is finally dried in a vacuum chamber at room-temperature under vacuum.
- the TEM (transmission electron micrograph) image of about 6 nm hcp cobalt nanocrystals is shown in Figure 3.
- a TEM image of about 8.5 nm, ⁇ -Mn-type cobalt particles is shown in Figure 4.
- nanocrystals in each case are very uniform in size and the particles are separated from each other by a layer of oleic acid coordinated on the surface.
- Decomposition of cobalt carbonyl gives high quality fcc cobalt nanocrystals.
- a terrace-like multilayer is shown of 8 nm monodisperse fcc cobalt nanocrystals on an amorphous carbon film at room temperature.
- This three- dimensional ordering is only possible with monodisperse particle systems of extremely uniform size and shape.
- the particles have a tendency to self-assemble into multilayer terrace superlattice structure due to attractive magnetic and van der Waals interactions among the particles.
- Cobalt particles prepared in accordance with the present invention have shown a high degree of ordering.
- the nanocrystals tend to self-organize into a hexagonal close packing (hcp) structure.
- the TEM images of the particles shows that the distance between the centers of the cobalt cores amount to approximately 3.5 nm.
- the chain length of oleic acid is approximately 2.5 nm.
- an approximately 3.5 nm separation represents that the protective mantels on the particle surface entangle each other.
- Oleic acid around the particles can be replaced by a variety of other acids such as 1,2-hexadienoic acid and polybutadiene dicarboxylic acid.
- polyvinylpyrrolidone can be chosen as another kind of stabilizing ligand because it contains an acetylamide group that is a basic unit in DNA, polypeptide or other biomolecules.
- PVP polyvinylpyrrolidone
- results have shown that PVP can readily replace oleic acid to form PVP-protected particles.
- the superlattice formed with the oleic acid as a ligand now disappears.
- the particles were well-dispersed in a typical polymer linkage pattern, as shown in Figure 8, indicating that particles prepared in accordance with the present invention have great potential in biological labeling and imaging. Additionally, the ready solubility of the particles is desirable for magnetic separation of biological products.
- the sample was dissolved either with pentane or hexane (e.g., using oleic acid as a stabilizing ligand) or with dichloromethane (e.g., using PVP as a stabilizing ligand) and loaded into a high-quality quartz tube.
- SQUID Quantum Design super conducting quantum interference device
- the particles with size ranging from about 3 nm to about 10 nm are super-paramagnetic at room temperature. However, the super-paramagnetic properties are blocked at low temperature.
- the ferromagnetic properties of the particles can be examined via their hysteresis behavior.
- the M-H (e.g., magnetization vs. magnetic field strength) hysteresis loop is recorded at 5°K under a field up to 1.0 T. Size-and temperature-dependent hysteresis curves are presented in Figure 10.
- the coercivity reaches 159.2 kA/m (2000 Oe), whereas as the particle size decreases from approximately 9 nm to approximately 6 nm and further to approximately 3 nm, their coercivities are reduced from approximately 71.4 kA/m (897 Oe) to approximately 23.2 kA/m (291 Oe) and down to approximately 17.4 kA/m ((219 Oe), respectively.
- the hysteresis of particles with sizes less than approximately 9 nm disappears, while particles having a size of approximately 11 nm still show ferromagnetic behavior with an Hc of approximately 10.7 kA/m (135 Oe) (e.g., see Figure 10).
- the present inventors have been successful in extending the inventive synthetic method to other metal systems.
- monodisperse fcc Ni nanocrystals and more importantly, monodisperse, Co-Pt intermetallic particles and alloy nanoparticles such as Co-Ni and Ni-Fe particles (e.g., up to approximately 20 nm in size), have been made by the reduction of relative metal acetate, or metal acetylacetonate.
- Ni-Fe particle materials are used in giant magnetoresistive heads.
- Co-Pt alloy particles are known as particle for "ultra-high density recording media". Making more uniform and well-isolated Co-Pt alloy particles is an important object of the present invention, and the inventive method contributes to making monodisperse Co-Pt nanocrystals.
- the present invention achieves solution phase, high temperature reduction of metal salts and decomposition of neutral organometallic precursors which lead to metal nanoparticles.
- Stabilization of the particles is reached by combination, for example, of oleic acid and trialkylphosphine.
- Monodisperse nanocrystals can be separated by size selective precipitation.
- the individual particles are well-isolated from each other by an organic layer. Thus, intergranular exchange among these particles is greatly reduced.
- Figure 11A highlights the inventive phase synthesis technique employing an injecting of reagents to control the nucleation of nanoparticles.
- Figure 11B is a standard representation of the conditions necessary to produce monodisperse colloids to describe the growth of monodisperse micron sized sulphur colloids. Its critical feature is the temporally discrete nucleation event followed by slow growth on the nuclei. By designing a series of specific chemical procedures which conform to this general reaction outline, the present inventors have optimized the conditions for the growth of monodisperse magnetic nanocrystals.
- Figure 12 schematically show the formation of ordered arrays of nanoparticles by the evaporation of a colloidal dispersion onto a solid substrate.
- Figure 13 depicts the basic steps in size selective precipitation as described below in the Examples.
- Figure 14 displays the extreme uniformity of the fcc cobalt particles which result from the innovations presented.
- the high magnification insets in the TEM image of Figure 14 clearly show the hexagonal close-packing of the nanocrystals, and displays one vacancy in the superlattice which confirms the three-dimensional structure of the assembly by revealing the positions of the underlying particles.
- Figure 15 illustrates a flowchart of the inventive process 150, which represents one of the methods, and Figure 16 illustrates a second method in the flowchart 160.
- the inventive method of forming nanoparticles includes a first step 1501 of forming a metal precursor solution together with a surfactants solution.
- the metal precursor solution is formed from a transition metal.
- the metal precursor solution may be formed from a complex or a salt of the transition metal.
- the metal precursor solution may be injected into the surfactants solution or vice versa, as described above and below in the Examples.
- the surfactant solution may be preformed at a predetermined temperature (e.g., optimally higher than room temperature). Forming the metal precursor solution and the surfactant solution may be performed at room temperature or at an elevated temperature of between approximately 100°C to 300°C and most preferably about 240°C.
- step 1502 the mixture (e.g., the metal precursor solution and surfactants solution) is heated to a temperature of between approximately 100°C to 300°C, and most preferably about 240°C.
- a reducing agent is introduced (e.g., rapidly injected) to the metal precursor solution and surfactants solution.
- step 1504 the mixture is cooled and a flocculent is added, as described above and below in the Examples, to the colloidal dispersion, to cause nanoparticles to precipitate out of solution without permanent agglomeration.
- step 1505 the precipitate (e.g., particles) is separated.
- a solvent e.g., an aprotic hydrocarbon solvent
- redissolve e.g., redisperse or repeptize the nanoparticles
- step 1507 it is determined whether the size distribution is acceptable. If so, the process ends. If the size distribution is not acceptable, steps 1504-1507 may be repeated as desired to narrow the size distribution.
- Figure 16 illustrates a flowchart of another method of the inventive process of forming nanoparticles which includes a first step 1601 of forming a metal precursor solution from a transition metal.
- the metal precursor solution may be formed from a complex or a salt of the transition metal.
- Such a step may be performed at room temperature or at an elevated temperature of between approximately 100°C to 300°C, and most preferably about 240°C.
- a surfactant solution is formed and heated, as described above and below in the Examples.
- the surfactant solution may be preformed at a predetermined temperature (e.g., optimally higher than room temperature).
- the metal precursor solution is introduced (e.g., rapidly injected) to the hot surfactant solution. It is noted that instead of introducing (e.g., rapidly injecting) the metal precursor solution to the surfactant solution, the surfactant solution could be introduced (e.g., rapidly injected) to the metal precursor solution.
- step 1604 the mixture (e.g., colloidal dispersion) is cooled, and a flocculent is added thereto, as described above and below in the Examples, for separating the precipitate (particles).
- a flocculent is added thereto, as described above and below in the Examples, for separating the precipitate (particles).
- step 1605 the precipitate is separated. Specifically, the particles (nanoparticles) are precipitated out of solution without permanent agglomeration.
- a solvent e.g., preferably an aprotic hydrocarbon solvent
- a solvent is added to the precipitate to redissolve the same (redisperse or repeptize the nanoparticles).
- step 1607 it is determined whether the size distribution is acceptable. If so, the process ends. If the size distribution is not acceptable, steps 1604-1607 may be repeated as desired to narrow the size distribution.
- the method of the present invention offers a unique and unobvious approach to producing monodisperse transition metal nanostructures, as is illustrated by the following examples.
- Monodisperse 6 nm hcp cobalt nanoparticles were synthesized as follows. First, cobalt acetate tetrahydrate / oleic acid / PR 3 / phenylether in a ratio of 1 mmol/ 2 mmol / 2 mmol / 10 mL were mixed under a nitrogen atmosphere in a sealed vessel (e.g., as shown in Figure 11A), and were heated to 240°C over a period of ⁇ 30 minutes. It is noted that a complete dissolution of the metal precursor is indicated by the formation of a clear, dark blue solution.
- methanol was added in a dropwise manner (e.g., as shown in Figure 12) until an air-stable magnetic black precipitate began to separate from the solution. Then, the precipitate was separated by centrifugation (e.g., as shown in Figure 12) or filtration after which the supernatant was discarded, and the black waxy magnetic precipitate was redispersed in hexane in the presence of approximately 100 to 500 microliters of oleic acid. Size-selective precipitation was performed by titrating the hexane solution with a short chain alcohol (e.g., methanol, ethanol, propanol, and/or isopropanol, but preferably ethanol).
- a short chain alcohol e.g., methanol, ethanol, propanol, and/or isopropanol, but preferably ethanol.
- Magnetic transition metal intermetallics e.g., CoPt, Co 3 Pt, etc.
- alloy particles such as, for example, Co/Ni, Ni/Fe or the like
- the phase of the intermetallic particles and the composition of the alloy can be easily adjusted by changing the molar ratio of starting metal salts.
- Nickel acetate tetrahydrate, iron acetate, and platinum acetylacetonate were used as Ni, Fe, and Pt sources, respectively.
- Monodisperse 8 nm fcc cobalt nanocrystals were prepared as follows. First, under a nitrogen atmosphere, oleic acid / PR3 / phenylether in the ratio of 1 mmol / 1 mmol / 20 mL, respectively, were mixed and heated to 200°C over a period of ⁇ 30 min. A phenyl ether solution dicobalt octacarbonyl (1 mmol) was injected to the hot mixture as it was undergoing vigorous stirring (e.g., with either a magnetic stir-bar or a mechanical device). A black solution was formed instantly, indicating the decomposition of the carbonyl and the formation of cobalt particles.
- the solution was stirred vigorously at 200°C for a total of 15 minutes, and then cooled to room temperature.
- Dropwise addition of methanol e.g., as shown in Figure 12
- methanol e.g., as shown in Figure 12
- the air-stable magnetic black precipitate produced was separated by centrifugation or filtration, and the supernatant was discarded.
- the black magnetic waxy product was redispersed in hexane in the presence of approximately 100 to 500 microliters of oleic acid. Size-selective precipitation was performed by titrating the hexane solution with ethanol.
- Example 2 In contrast to the procedure of Example 1, the procedure of Example 2 provides access to particles with different crystal phases. Additionally, the method of Example 2 provides a better route to different crystal structures and better initial particle size distribution than Example 1, which allows the isolation of monodisperse particles in fewer recursive steps of size selective precipitation.
- the improved initial size distribution is attained because the carbonyl decomposition route more closely approaches the idealized growth curve for monodisperse colloids depicted in Figure llB.
- the kinetics of the carbonyl decomposition are much faster than the polyol reduction producing a more temporally discrete nucleation event, and better separation of the nucleation and growth stages of the reaction.
- the extreme uniformity of the material produce using the carbonyl decomposition procedure is evident in the TEM image of Figure 14.
- an ensemble of 8-nm. diameter fcc cobalt particles is seen organized into a regular three-dimensional array (e.g., also referred to as a colloidal crystal or nanocrystal superlattice).
- a statistical analysis of the particles in the images places a measurement limited standard deviation in particle size to be less than 5% in diameter.
- the striking regularity of the assembly is a clear indication of the uniformity of the constituent particles.
- Monodisperse 10 nm cubic phase cobalt nanoparticles were produced as follows. First, CoCl 2 (anhydrous) / oleic acid / tributylphosphine / n-octylether in a ratio of 1 mmol / 1 mmol / 3 mmol / 20 mL, respectively, were mixed under a nitrogen atmosphere, and heated to 200°C. LiBHEt 3 (superhydride) (2 mmol) was injected into the hot blue solution under vigorous stirring. A black/brown solution was formed instantly, indicating the reduction of CoCl 2 and the formation of cobalt particles. The solution was stirred at 200°C for approximately 15 minutes and cooled to below 60°C.
- Example 3 yields yet another crystal phase of cobalt particles, thereby allowing more materials choices for various applications.
- This material displays a crystal symmetry of the ⁇ -phase of manganese.
- This novel phase of cobalt can be transformed subsequently into either the hcp or fcc crystal structures by controlled annealing. Heating the ( ⁇ -manganese) nanoparticles at temperatures lower than 400°C converts the material to predominantly hcp particles (e.g., hcp is the preferred bulk phase below 425°C). If the annealing is performed at temperatures above 400°C, the nanoparticles produced by the process of Example 3 convert to fcc particles (e.g., the stable bulk phase at temperatures above 425°C).
- the diffraction patterns of figure 2B document the structural transitions.
- the kinetics of the alkylborohdryide reduction and rate are similar to the carbonyl decomposition (method of Example 2), but are much faster than the polyol reduction (e.g., method of Example 1), thereby producing a temporally discrete nucleation event, and good separation of the nucleation and growth stages of the reaction.
- the extreme uniformity of the material produced using the superhydride reduction procedure is evident in the TEM image of Figure 4.
- an ensemble of 8-nm. diameter cobalt particles is seen organized in to a regular three-dimensional array (e.g., also referred to as a colloidal crystal or nanocrystal superlattice).
- the statistical analysis of the particle in the images places a measurement- limited standard deviation in particle size to be less than 5% in diameter.
- the process was as follows. First, cobalt particles synthesized as above (e.g., as in any of methods of Examples 1, 2, or 3) were redispersed in phenyl ether under N 2 . AgNO 3 1,2-dodecanediol (one equivalent of Ag>NO 3 ) were added to the dispersion. The mixture was stirred mechanically or magnetically at room temperature for about 10 minutes to ensure complete dissolution of the reagents. Then, the temperature was slowly raised to 100°C in a period of 20 minutes with continuous stirring and held at 100°C for 10 minutes.
- the mixture After being cooled down to room temperature, the mixture was treated with methanol, which produced an air-stable black-brown precipitate, and the mixture underwent centrifugation. The supernatant was discarded after centrifugation. The product was redispersed in hexane in the presence of about 100 - 500 microliters of oleic acid. Size-selective precipitation was performed by titrating the hexane solution with ethanol.
- Pd- and Pt-coated Co particles and other ferromagnetic metal-based e.g., such as Ni-based
- over-coated nanocrystals Merely by substituting the AgNO 3 for Pd(acetate), Pt(acetate) and nickel acetate, respectively.
- the resulting particles each have a surface shell of the less chemically-active metal which improves the corrosion resistance of the particles and allows new chemical groups to be bound to the surface.
- the present invention provides a method for the chemical synthesis of magnetic transition metal nanocrystals (colloids) and their assembly into two- and three-dimensional ordered lattices and a method for the use of the dispersed colloids and ordered lattices.
- the invention employs these unusually uniform dispersed magnetic nanocrystals with significant benefit in a range of applications where currently less uniform colloidal or granular magnetic material is employed.
- the uniform magnetic colloids can be utilized in the dispersed state as magnetic ink or in engineering applications including magnetorheological fluids (e.g., ferrofluids), as electromagnetic tags for interrogation of composite materials, as remote heat sources when under the influence of electromagnetic radiation near the ferromagnetic resonance frequency of the individual particles, and as the active light modulator in a magnetopheretic display.
- magnetorheological fluids e.g., ferrofluids
- electromagnetic tags for interrogation of composite materials
- remote heat sources when under the influence of electromagnetic radiation near the ferromagnetic resonance frequency of the individual particles
- active light modulator in a magnetopheretic display.
- dispersed magnetic nanocrystals as contrast-enhancing agents in magnetic resonance imaging (MRI), remote heat sources for hyper-thermal destruction of tissue under the influence of an external electromagnetic field, an externally-triggered drug delivery vehicle, selective magnetic labels in high gradient magnetic separation of purification/isolation biomolecules and cellular products, and for use in medical diagnosis through the selective isolation of biological products which are considered indicative of the presence of disease or bodily dysfunction.
- MRI magnetic resonance imaging
- remote heat sources for hyper-thermal destruction of tissue under the influence of an external electromagnetic field
- an externally-triggered drug delivery vehicle selective magnetic labels in high gradient magnetic separation of purification/isolation biomolecules and cellular products, and for use in medical diagnosis through the selective isolation of biological products which are considered indicative of the presence of disease or bodily dysfunction.
- Organized assemblies of the magnetic nanocrystals have significant potential as high density magnetic recording media (e.g., tapes, flexible disks, rigid disks, magnetic smart cards and the like). Close-packed assemblies of these magnetic nanocrystals are envisioned as the active magnetoresistive medium in two components of nonvolatile magnetic storage technologies, as the magnetoresistive medium in magnetic sensors (e.g., read heads) exploiting the modulation spin-dependent hopping/tunneling between neighboring nanocrystals in the presence of a modulated external magnetic field or in proximity to a magnetic encoded pattern.
- magnetic sensors e.g., read heads
- Assemblies of uniform magnetic nanocrystals also are envisioned as the active elements in the channel of transistors for non-volatile magnetic random access memory in which the spin-dependent (magnetoresistive) and hysteretic properties of the nanocrystals are simultaneously exploited.
- a strong magnetic field e.g., produced by write pulses or the like
- on-chip current flow is generated by on-chip current flow which is sufficient to orient the magnetic polarization of the nanocrystals in the channel.
Claims (29)
- Procédé de formation de nanoparticules, comprenant les étapes consistant à :former une solution de précurseur de métal à partir d'un métal de transition,introduire ladite solution de précurseur d'un métal dans une solution d'agent tensioactif comprenant une combinaison d'un stabilisant organique et d'une trialkylphosphine pour protéger lesdites nanoparticules, etledit stabilisant organique étant un composé organique à chaíne longue de la forme R-X, où R est un membre choisi à partir du groupe constitué de 1) une chaíne d'hydrocarbures sous une forme droite ou ramifiée, ladite chaíne d'hydrocarbures comprenant 6 à 22 atomes de carbone, et 2) une chaíne fluorocarbonée sous une forme droite ou ramifiée, ladite chaíne fluorocarbonée comprenant 6 à 22 atomes de carbone, et où X est choisi parmi l'acide carboxylique, l'acide phosphonique, l'acide phosphinique, l'acide sulfonique, les acides sulfiniques et le thiol,ajouter un floculant pour amener des nanoparticules à précipiter hors de la solution sans agglomération permanente, etajouter un solvant d'hydrocarbure pour l'une d'une redispersion et d'une repeptisation desdites nanoparticules.
- Procédé selon la revendication 1, dans lequel ladite étape de formation d'une solution d'un précurseur de métal comprend la formation d'une solution d'un précurseur de métal sous forme d'un complexe du métal de transition à une première température, ladite première température étant la température ambiante.
- Procédé selon la revendication 1, dans lequel ladite étape de formation d'une solution de précurseur d'un métal comprend une étape consistant à former une solution de précurseur d'un métal à partir d'un sel du métal de transition, d'un agent tensioactif ionique, et d'un solvant inerte approximativement à 240°C.
- Procédé selon la revendication 1, dans lequel ladite étape de formation d'une solution de précurseur d'un métal est exécutée à une première température et ladite étape d'introduction dudit précurseur d'un métal dans ladite solution d'agent tensioactif est exécutée à une seconde température.
- Procédé selon la revendication 4, dans lequel ladite première température est une température ambiante et ladite étape d'introduction est exécutée à une température sensiblement à l'intérieur d'une plage d'approximativement 200°C jusqu'à approximativement 300°C.
- Procédé selon la revendication 5, dans lequel ladite étape d'introduction est exécutée à une température d'environ 240°C sensiblement.
- Procédé selon la revendication 4, dans lequel ladite première température est une température sensiblement à l'intérieur d'une plage d'approximativement 200°C jusqu'à approximativement 300°C, et ladite seconde température est inférieure à 240°C.
- Procédé selon la revendication 7, dans lequel ladite première température est sensiblement autour de 240°C.
- Procédé selon la revendication 1, dans lequel un diol à chaíne longue est utilisé pour réduire des sels de cobalt afin de fournir des nanoparticules de cobalt étroitement compactées sous forme hexagonale (hcp),
dans lequel le diol comprend l'un du 1,2-octanediol, du 1,2-dodécanediol et du 1,2-hexadécanediol,
dans lequel du tétrahydrate d'acétate de cobalt et de l'acétylacétonate de cobalt sont utilisés comme source de cobalt. - Procédé selon la revendication 1, dans lequel ladite solution de précurseur d'un métal comprend un système métallique comprenant essentiellement l'un de Ni(Ac)2-4H2O, NiCl2, Cu(Ac)2H2O, Cu(acac)2, Pd(Ac)2, PdCl2, Ag(Ac), AgNO3, et PtCl2.
- Procédé selon la revendication 1, dans lequel lesdites nanoparticules comprennent des nanoparticules à base de cobalt et ladite solution d'agent tensioactif comprend du dicobaltoctacarbonyle, une décomposition dudit dicobaltoctacarbonyle fournissant des nanocristaux de cobalt cubiques à face centrée (fcc).
- Procédé selon la revendication 1, dans lequel ladite étape d'addition d'un solvant d'hydrocarbure comprend une réduction du chlorure de cobalt par un super hydrure résultant en la formation de nanoparticules de cobalt en phase cubique,
dans lequel ledit super hydrure est l'un du tétrahydrofurane, du phényléther et de l'octyléther. - Procédé selon la revendication 12, dans lequel ledit système métallique comprend l'un de Co(Ac)2-4H2O, NiCl2(H2O), NiAc2-4H2O, CuCl2 (H2O), PdCl2, PdAc2, AgAc, AgNO3 et Ptcl2.
- Procédé selon la revendication 1, dans lequel une coréduction des deux sels métalliques fournit un composé intermétallique comprenant l'un de Co3Pt, CoPt, CoPt3, Fe3Pt, FePt, FePt3, et des alliages comprenant l'un d'un alliage binaire, y compris l'un de Co/Ni, Ni/Fe et Co/Fe, et d'un alliage ternaire de particules de Co/Fe/Ni.
- Procédé selon la revendication 1, dans lequel une réduction séquentielle d'un sel métallique et d'un sel d'un métal noble est exécutée pour obtenir des particules revêtues d'un métal noble.
- Procédé selon la revendication 1, dans lequel lesdites nanoparticules comprennent un acide et un ligan d'acétylamide autour d'elles.
- Procédé de formation de nanoparticules selon la revendication 1, dans lequel ladite étape de formation comprend la formation d'une solution de précurseur d'un métal sous forme d'un complexe d'un métal de transition à une première température et la formation d'une solution d'agent tensioactif à une seconde température supérieure à ladite première température, ladite solution de précurseur d'un métal étant introduite dans ladite solution d'agent tensioactif pour former un mélange, ledit floculant étant ajouté audit mélange pour amener des nanoparticules à précipiter hors de la solution sans agglomération permanente.
- Procédé selon la revendication 17, dans lequel ladite solution d'agent tensioactif comprend un solvant inerte comprenant un solvant à point d'ébullition élevé présentant un point d'ébullition sensiblement à l'intérieur d'une plage d'approximativement 200°C à approximativement 300°C, et ladite seconde température est approximativement de 240°C.
- Procédé selon la revendication 17, dans lequel ladite solution d'agent tensioactif comprend au moins un agent tensioactif ionique, un agent tensioactif neutre, et un solvant inerte.
- Procédé selon la revendication 19, dans lequel ledit solvant comprend de l'éther, et
dans lequel ladite première température est la température ambiante et ladite seconde température est approximativement de 240°C. - Procédé de formation de nanoparticules selon la revendication 1, dans lequel ladite solution de précurseur d'un métal est formée sous forme d'un sel d'un métal de transition, et ladite étape d'introduction comprend l'injection rapide de ladite solution de précurseur de métal dans ladite solution d'agent tensioactif.
- Procédé selon la revendication 21, dans lequel ladite étape de formation d'une solution de précurseur d'un métal comprend la formation de la solution de précurseur d'un métal à partir du sel du métal de transition, d'un agent tensioactif ionique, d'un agent tensioactif neutre, et d'un éther inerte, à une température sensiblement à l'intérieur d'une plage d'environ 100°C à environ 300°C.
- Procédé de formation de nanoparticules comprenant les étapes consistant à :former une solution de précurseur d'un métal à une première température,introduire un agent de réduction à une seconde température dans ladite solution de précurseur d'un métal,ajouter un floculant pour amener des nanoparticules à précipiter hors de la solution sans agglomération permanente, etajouter un solvant d'hydrocarbure pour l'une d'une redispersion et d'une repeptisation desdites nanoparticules,
dans lequel une granulométrie est commandée en modifiant un rapport dudit acide et de ladite trialkylphosphine,
l'acide étant RCOOH, R étant égal à l'un de C12H24, C17H34 et C21H42 et la trialkylphosphine étant PR3, R étant l'un du phényle, C2H5, C4H9 et C8H17. - Procédé selon la revendication 23, dans lequel ladite étape de formation d'une solution de précurseur d'un métal comprend la formation d'une solution de précurseur d'un métal à partir d'un sel d'un métal de transition, d'un agent tensioactif ionique, et d'un solvant inerte à une température dans une plage d'approximativement 100°C à approximativement 300°C.
- Procédé selon la revendication 1 ou 23, dans lequel ledit solvant d'hydrocarbure comprend l'un d'un phényléther et d'un N-octyléther, lesdites nanoparticules étant des nanoparticules à base de cobalt, et
dans lequel une plage de ladite première température est sensiblement entre approximativement 100°C et approximativement 300°C. - Procédé selon la revendication 1, dans lequel lesdites nanoparticules comprennent des particules à base de cobalt.
- Procédé de formation de nanoparticules selon la revendication 23, dans lequel ladite étape de formation comprend la formation d'une solution de précurseur d'un sel de métal contenant un agent tensioactif dans un solvant non réactif, ledit agent de réduction réduit le sel de métal in situ pour produire des particules métalliques colloïdales, ledit procédé comprenant en outre l'étape consistant à séparer les sous-produits de la synthèse qui restent en solution, ledit solvant d'hydrocarbure étant ajouté aux nanoparticules précipitées.
- Procédé selon la revendication 27, dans lequel l'agent tensioactif comprend au moins l'un d'une alkylphosphine et d'un stabilisant organique, ledit stabilisant organique comprenant un composé organique à chaíne longue de la forme R-X, où R est un membre choisi parmi le groupe constitué de 1) une chaíne d'hydrocarbures sous une forme droite ou ramifiée, ladite chaíne d'hydrocarbures comprenant 6 à 22 atomes de carbone, et 2) une chaíne fluorocarbonée sous une forme droite ou ramifiée, ladite chaíne fluorocarbonée comprenant 6 à 22 atomes de carbone, et où X est choisi parmi l'acide carboxylique, l'acide phosphonique, l'acide phosphinique, l'acide sulfonique, les acides sulfiniques et le thiol.
- Procédé selon la revendication 28, dans lequel ladite alkylphosphine est une alkylphosphine tertiaire et ledit stabilisant organique est l'acide oléique.
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US09/127,005 US6262129B1 (en) | 1998-07-31 | 1998-07-31 | Method for producing nanoparticles of transition metals |
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EP (1) | EP0977212B1 (fr) |
JP (1) | JP3258295B2 (fr) |
KR (1) | KR100378027B1 (fr) |
CN (1) | CN1328735C (fr) |
AT (1) | ATE233938T1 (fr) |
DE (1) | DE69905663T2 (fr) |
SG (1) | SG83738A1 (fr) |
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- 1999-07-20 SG SG9903475A patent/SG83738A1/en unknown
- 1999-07-21 EP EP99305759A patent/EP0977212B1/fr not_active Expired - Lifetime
- 1999-07-21 AT AT99305759T patent/ATE233938T1/de not_active IP Right Cessation
- 1999-07-21 DE DE69905663T patent/DE69905663T2/de not_active Expired - Lifetime
- 1999-07-26 JP JP21071699A patent/JP3258295B2/ja not_active Expired - Fee Related
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2004054923A1 (fr) * | 2002-12-16 | 2004-07-01 | Agency For Science, Technology And Research | Nanocristaux ternaires et quaternaires, leurs procedes de production et leurs utilisations |
US8668848B2 (en) | 2005-01-14 | 2014-03-11 | Cabot Corporation | Metal nanoparticle compositions for reflective features |
WO2009133446A1 (fr) * | 2008-04-28 | 2009-11-05 | Tata Chemicals Limited | Procédé de fabrication de nanoparticules d'argent |
US8852316B2 (en) | 2008-04-28 | 2014-10-07 | Tata Chemicals Limited | Process for the preparation of silver nano particles |
US8383014B2 (en) | 2010-06-15 | 2013-02-26 | Cabot Corporation | Metal nanoparticle compositions |
Also Published As
Publication number | Publication date |
---|---|
ATE233938T1 (de) | 2003-03-15 |
SG83738A1 (en) | 2001-10-16 |
CN1328735C (zh) | 2007-07-25 |
DE69905663D1 (de) | 2003-04-10 |
EP0977212A3 (fr) | 2000-07-05 |
DE69905663T2 (de) | 2003-11-20 |
US6262129B1 (en) | 2001-07-17 |
JP2000054012A (ja) | 2000-02-22 |
EP0977212A2 (fr) | 2000-02-02 |
JP3258295B2 (ja) | 2002-02-18 |
CN1243775A (zh) | 2000-02-09 |
KR100378027B1 (ko) | 2003-03-29 |
KR20000011546A (ko) | 2000-02-25 |
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